DE1608167A1 - Magnetic alloy - Google Patents

Description

Priority December 28, 1966, No. 85 381/66, Japan.

The invention relates to a magnetic alloy and especially on a magnetic alloy with a rectangular Course of its hysteresis curve, so that the alloy for Cores can be used in magnetic amplifiers.

Cores for magnetic amplifiers that are to be used in magnetic devices for automatic control or in instruments v / ie magnetic amplifiers (transducer amplifiers) or in a magnetic multivibrator must have a hysteresis curve that is as square as possible. In order to obtain the effective magnetic properties, it is an anisotropic material has formed into a ring-shaped core such that no air gap arises in the Megnetlinienverlauf that an unfavorable influence on the rectangular profile of the

Has hysteresis curve of the nucleus. '

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Mn material such as oriented © 50 ~ Permalloy or an oriented Silicon steel sheet, its orientation during rolling and tempering has been produced, are preferably used as the cores.

From a consumer standpoint, however, toroidal cores have dare the difficult winding process and its poor fill factor, when used in circuits, certain disadvantages over conventional laminated cores that are E-I-shaped have been punched out. Therefore the development of stamped laminated cores with * excellent rectangular hysterosis properties particularly desirable.

Magnetic properties required for cores, which in magnetic amplifiers or magnetic HuItivibrato- '· can be summarized as follows:

1. Large magnetic flux density.

When a core material having a large magnetic flux density, a small Querschnittsfläcbe of the core for a given magnetic flux may be sufficient and dia size of the device characteristic can be greatly decreased *

2 « small coercive force.

. A small coercive force is not advantageous for core material because it requires a proportionally large excitation current. Furthermore, large coersitive forces increase energy loss in an alternating magnetic current and lead to it

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a rise in temperature in the core.

3 · Rectangular course of the llysteresis curve.

The core material for magnetic amplifiers or magnetic föultivibratoren must have such a course of the hysteresis curve possess that the rise of the magnetization curve is sharp and that the approaching parts of the curve © run flat until saturation of the lagnetization.

In general, a magnetic amplifier must have a rectangular ratio Br / Bm or 3k / Bn, greater than O _t 9i, if Br is the remaining magnetic flux density, Bk is the magnetic plus density at the inflection point of the magnetization curve and Bm is the maximum magnetic flux density »

4. Small temperature coefficient of the magnetic properties.

Metallic magnetic substances have a distinct advantage with regard to their low temperature coefficient of magnetic properties compared to ferrite (magnetic oxide substances). Although even metallic substances have different temperature coefficients depending on the composition of the alloy, so should the change in magnetic Properties of the cores naturally be as low as possible when the latter are used as circuit elements used in automatic control equipment or in instruments.

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5. High specific electrical resistance.

When the core is in a magnetic alternating current field orders v / ird, the eddy current loss generated is reversed proportional to the specific electrical resistance of the core material. Therefore should be the specific electrical l / iderstand bo be large as humanly possible.

6. Slight change in magnetic properties due to external tensions «,

Though a core material with small coercive force and rectangular The course of the hysteresis curve tends to be magnetic For practical reasons, changing properties in the event of external stress is the smallest possible change the magnetic properties are desirable.

Ee is therefore an object of the invention to provide a new magnetic Specify alloy with an excellent rectangular shape of the hysteresis curve. The new alloy fulfills in excellent, Way the above mentioned requirements. It can easily be used to produce punched elements that can be easily let wrap.

Vegetables of the invention, the magnetic alloy essentially consists of a Fe-Co-Ni alloy system to which was less than 5 wt.% Mo or Cu is added, and the Curie point higher than 620 ° C, extending through the magnetic annealing treatment can be effectively influenced.

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Fig. 1 shows the Ourie-i-points of the Fe-Go-Ni alloy, applied .gen in the ternary phase diagram of Fe, Co, Ki.

Fig. 2 shows the spontaneous magnetization of the same alloy ' stanchions which are shown in a manner similar to that in FIG.

Fig. 3 shows the Xocitive Forces of the same alloys that are plotted in a similar manner to that in FIG.

Figure 4 is a plan view of a misshapen core member which 3US made of the magnetic alloy according to the invention has been.

Fig. 5 is an explanatory drawing for the magnetic annealing treatment to represent a core, which by lamination or laying on top of one another of Kernalementen. according to Fig. 4 arise igt.

Fig. 6 is a perspective view of a core constructed by a package of U-shaped kernel elements according to the invention has been.

Fig. 7 shows part of a magnetization curve, including the definition to explain the rectangular ratio Br / Bm or Bk / Bm.

The applicant has made thorough studies of the Fe-Go-Hi system made in order to develop a core set from it

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can whose eysteresis curve is rectangular and that all six requirements mentioned above are met. It can also subjected to a magnetic terapering treatment in order to further improve the shape of the rectangular hysteresis curve. ! Furthermore, the shapes of core elements were examined, such as the U-shape, ring-shape, and the like. In the following, the magnetic Properties of the Pe-Co-Ki-üysteas based on ternary Pha sendiagramnen explained as a basis for the invention.

Figures «1» 2 and 3 show the Curie points, spontaneous magnetization (in Gauss) and coercive forces (in Oersted) of Fe-Co-Ki alloys. These drawings are derived from the book "Ferromagnetic ¹ by RM Bozorth, published by D. Van Nostrand Co., 1951" From the drawings one can readily see that with a Ni-Ilenge greater than 50 wt. JS the Ourie points increase when the amount of Co increases. On the other hand, when the amount of I ^? e increases over 30 wt. Ja, the Curie point drops rapidly.

When Co is 4.30 ^e £ and Fe <10 ^C J> , the spontaneous magnetization of the alloys largely decreases, and when Co> 30 % and Fe;> 10 % , the coercive forces of the alloys are high.

It can also be estimated that the closer the atomic ratio of Ni and Co plus Fe is 1, the greater the induced magnetic anisotropy, because of the magnetic tempering treatment and that the higher the Curie point of an alloy, the lower the temperature coefficient of its magnetic ones Properties is.

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In order to achieve the objects of the invention, the possible ranges of the composition of an alloy v / ie of the Fe-Go-Hi system are given in such a way that Fe plus Go <50 #, 10 JS <Fe -C30 $ and an amount of nickel is not is so large, preferably less than 80 wt. # , because of the practical amount for spontaneous magnetization, the amounts of Go and l? e do not include O $.

Increasing numbers of Go Xm Fe-Go-Hi systems lead to an increase in Gurie points and an improvement in the induced magnetic anisotropy, while an increase in Go not only makes its coercive force high, but also makes its magnetostrictive coefficient so high that its magnetic properties change as a result of an external voltage. As a result, the amount of cobalt should be limited to less than 50 wt. Yes »

On the other hand, if the amount of cobalt in the alloy is too small is, the Curie point and the spontaneous © magnetization of the Alloy decreases considerably and you can no longer use good ones calculate magnetic properties. Therefore, with the inventive Alloy the amount of cobalt is greater than at least 5 wt. # Be. The desired © hangs can range from 7 to ± 12 21 wt.

_E Fe-Go-Ki system is clear from the above considerations that a Zusaniniensatzmig nat ₉ in B © r®ieli 50 $ <£ Ki <80 fV <5 3 ^Go <30 # ^ ^d IC'tf <Fe <30 JS lies.

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However, these alloys have a disadvantage in that, because of their low electrical resistivity, they have the above do not fully meet the six requirements mentioned. They are therefore not for a magnetic device like one magnetic amplifier and a multivibrator, suitable where low energy losses are required.

In order to solve this problem of a low electrical resistivity, further investigations and experiments have been carried out. It has been shown that the addition of a suitable amount of molybdenum or copper causes an increase in the specific electrical resistance. The addition of Mo or Ou results in a better rectangular shape of the hysteresis curve. An object of the invention is not only to improve the magnetic properties of an alloy, v / ie its coercive force and its rectangular ratio, but also to increase the specific electrical resistance, which can be achieved by using less than 5 wt. % Molybdenum or copper, based on the alloy, is added. If a core material according to the invention is also used, a core provided for a magnetic amplifier or multivibrator can be U-shaped, although it nevertheless retains the desired rectangular shape of its hysteresis curve. Furthermore, the fill factor and the winding can be greatly improved or facilitated.

The invention is illustrated in more detail by means of the following examples.

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example 1

15 alloy samples, Gc 1 - 15 »explained in more detail in the table 1, were made by vacuum welding. For 2s elemental metals, electrolytic Fe, Go and Hi with very high purity were used «

A billet with a thickness of 10 mm was made from a Giissblook produced by hot processing, which in turn is tempered in the meantime and made into a plate with the final thickness of 0.3 mn has been processed by cold orphanage were ring specimens with an outside diameter of 45 mm and one Inside diameter of 35 mm punched out of the sheet metal and for used the following experiments.

In order to eliminate any internal stresses caused by the mechanical processing, the samples were ^{tempered at a temperature above 900 °} C. in a hydrogen atmosphere in order to oxidize them. prevent or contaminate samples from the atmosphere.

The samples were then subjected to the magnetic tempering treatment. First, a toroidal core was wound with such a winding that a Hegnet field was generated in it; he was again heated to 700 ⁰ O. The core was gradually cooled in the magnetic field from 700 ^{0 0} to 400 ⁰ U, the cooling speed about 25 ° 0 / 8td. ble 200 ° 0 / 8td. and the strength of

Magnetic field was about 2 -B Oersted

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Table 1 denotes the magnetic flux density BIO, a square ratio Br / BlO and BO.5 / BlO ₁ the coercive force He ₁ the Curie point Tc ₁ the specific electrical resistance ρ -cm) and a temperature coefficient of the magnetic

Flux density.α Blü Each sample, if it was ^{annealed for 2 hours at HOO 0} O, then heated again to 700 ° 0 and held at this temperature for 1/2 hour; it then went from 5 oersteds to 400 ⁰ G in a magnetic field with a cooling speed of 100 ° 0 / 3td. cooled down. In the table, α BIO is an average temperature coefficient between -20 ° C and + JO ⁰ O; BIO, Br / BlO, BO.5 / 310 uarden determined after the indication of the Ma ^ -netisierungswerte how they. are indicated in FIG. The extraordinarily good rectangular shape of the hysteresis curve can be shown by the fact that the values of Br / B10 and BO.5 / BIO are close to 100 % .

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sample Chemical together
Settlement in weight sP TABLE 1 Br / B10 B0.5 / B10
(ft) Hc
(Oe) 680 17.3 α -2.6 ■ B10 , 1 7Co-25Pe-Ni B10
(KG) 86.6 90.4 0.047 630 35.1 -2.5 X 10 ~ ⁴ 2 7Co-23Pe-2Mo-Ni 12.7 90.6 93.8 0.041 640 31.4 -2.5 ti 3 7Co-23Fe-2Cu-Hi 12.1 93.2 98.0 0.030 580 55.1 -2.5 It 4th 7Co-21Fe «-4Mo-Ni 12.2 68.6 81.3 0.105 600 44.0 -2.3 ti 5 7Co-21Fe-4Cu-Ki 11.0 75.5 87.5 0.066 690
640 .17.2
36.3 -2.2
-2.3 Ii 6th
7th 14Co-26Pe-Ni
14Co-24Pe-2Mo-Ni 11.3 88.9
91.3 92 ,?
95.0 0.038
0.033 650 31.0 -2.3 Il
It Ν »
O
e®
© ο 8th 14Co-24Fe-2Cu-Ni 13.8
12.8 92.4 95.1 0 _s 031 600 56.2 -2.4 η - »,
Ca » ^ _x 9 i4Co-22Fe-4Mo-Ni 13.0 80.7 85.4 0.092 620 46.5 -2.4 η O 10 14Co-22Pe-4Cu-Ni 11.4 88.3 92.3 0.043 710 18.4 -2.0 η (Eft 11 21Co-26Pe-Ki 11.5 Θ7.8 92.9 0.046 670 36.7 -2.1 ti 12th 21Go-24-I ^t e-2Mo-Ni 14.6 89.3 93.8 0.030 670 31.9 -2.1 it 13th 21Co ~ 24Fe-2Cu-! Ti 13.7 91.0 95.2 0.025 630 55.9 -2.3 Il 14th 21Co-22Pe-4Mo-Ni 13.9 85.8 91.1 0.040 640 45.1 -2.3 Il 15th 21Co-22Pe-4Cu-Ni 12.6 85.9 90.7 0.035 11
σ>
ο
co 12.9

From Table 1 it can be seen that although the ternary Alloys Pe-Oo-Ki of samples Kr. 1, 6 and 11 have higher Curie points and relatively good magnetic properties, however, the specific electrical resistance is considerably low.

Low specific electrical resistance causes one large V / irbelstrora loss in a nucleus that is exposed to an alternating current magnetic field is exposed. In contrast, Fe-Co-Ni-Mo show or Fe-Co-lIi-Cu alloys, which is a suitable amount Containing molybdenum or copper in addition to Pe, Co and Ki, have a high electrical resistivity. Samples No. 4 ·, 5 and are an exception. 9 »with the alloys having a Tc higher than

620 ⁰ C and have excellent magnetic properties.

To improve the rectangular shape of the hysteresis curve, the alloy should be effectively affected by magnetic annealing be that they have a powerful magnetic anisotropy

shows. It was found that the degree of influence on the »

magnetic annealing treatment of an alloy is an important one Affects the Gurie point of the alloy. föan can generally say that alloys with high Curie points show excellent magnetic properties.

In samples Kr. 4, 5 and 9, Hc is large and both 3r / B10 and B0.5 / B1C are small, although these samples have a composition that is in the range of Pe <£ 30, Co <30 #, Mo or Cu <4 % with the remainder being Hi. Your Curie points tend to be low

2 O 9 8 1 3, μ ν, ν _BAD Or ₁ Q _1n ^

to be lower than 620 ° G, since one from the-Fig. 1 can be seen that a small percentage of cobalt tends to make up the Cuiiie point to lower and also the addition of molybdenum or copper leads to lowering of Tc.

As a result, the amount of molybdenum or copper to be added should be chosen so that the Curie point of the alloys is higher than at least 62O ⁰ O. A temperature coefficient-α BIO of BIO of the Fe-Co-lü-Mor or Fe-Oo-Hi-Cu system is - (2.0-2.6 χ 10 ~ ') with an average value between -20 ° 0 and +30 ⁰ C. It is about half the value for common known materials used for ring-shaped cores, such as oriented 50-Perraalloy (50 # Hi-Fe alloy, α BIO «'- (5.5 χ 10 * " ^Zi ")) Supermalloy (5 # Mo - 79 # Ni-Fe alloy;. Α BIO β (6.0 χ ΙΟ " ⁴ )).

On the other hand, it can be seen that the samples with a higher Tc value? tend to have smaller absolute values for BIO. Among these samples, those with grief 2, 3t 7 » 8, 10, .12, 13, 14 and 15 the conditions according to which.BIO ■ 11,5KG (KGauss), Br / B10> 85 #, Hc <0.05 Oe, P> 30 uO and α BIO <2.5 κ 10 "". These samples have therefore proven to be quite suitable proved to be a core material with a rectangular course of the hysteresis curve to produce a magnetic Amplifier, a magnetic multivibrator and the like. suitable.

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Example 2

Two types of alloys have been identified on the influence of the tempering temperature examined as indicated in Table 2. The composition of the alloy samples corresponds to the samples Kr. 2 and 3 of table 1. /

X 2 hours. 2 Br / BlO (Si) Hc (Oe) X Il BlO (KG) 89.7 0.125 Tabel X It 11.0 89.8 0.065 Tempering conditions X I! 11.4 89.0 0.050 Sample 2 80O ⁰ O X Il 11.4 90.1 0.040 900 ° 0 X Il 11.6 8 ^, 5 0.031 1,000 ⁰ C X 2 hours. 11.7 80.5 0.033 1,100 ^° C X Il 11.7 91.7 0.055 1.2GO ⁰ C X Il 11.9 93.4 0.045 i 500 ° o X ir 11.9 92.8 0.038 Sample 3 800 ° C X Il 12.0 93.2 0.027 90C ° C X Il 12.1 86 _f 6 0.023 1,000 ⁰ C 12.1 82.6 0.020 1,100 ° C 12.1 1,200 ⁰ C 1,300 ⁰ C Example 3

The influence of the cooling speed in the magnetic field was one examined two alloys, whose composition the samples No. 2 and 3 correspond. The results are shown in Table 3.

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/ Γ

Table 3

Cooling conditions in: \ - en BIO (KG) Br / BlO (fr) Hc (Oe)

sample 2 2üO ° G / ötd. 11.5 78.1 0 , 055 10O ⁰ G / " 11.6 90.1 0 , 040 50 ⁰ C / " 11.7 90.5 0 , 032 sample 3 200 ° G / 8td. 11.6 88.6 0 , 0 ^ 5 100 ⁰ O / » 12.1 93.2 0 , 02? 3O ⁰ G / " 12.1 93.8 O , 026

The samples were initially kept at 700 ° C. for 30 minutes. Then they were cooled with different cooling speeds in the magnetic field from 5 Oersted to 400 ⁰ G, as indicated in Table 3 *

Example 4

Table 4 shows the magnetic properties of a Fe-Co-Ki base alloy when 2 # copper and transition metals such as molybdenum, chromium and vanadium are added. The samples were produced in the shape of a ring with a disk of 0.3 mm and tempered at about 1100.degree. For the magnetic annealing treatment, the samples were initially 30 Hin. maintained at 700 ⁰ C and then at a rate of 50 ° C per ätunde in a magnetic field of 5 Oer.-sted to cooled to 400 ° C.

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209813/026 6

Table 4- BlO (KG) 86.1
90.6
66.6
65.6 > Hc (Oe) Sample Ii r. Composition (weight #) 11.1
11.9
11.0
10.5 0.039
0.04-1
0-066
0.04-6 1
2
3 7 Co-21Fe ~ 2Mo-III
7Qo-21Fe-2Gu-tii
70o ~ 21Fe-2Cr-Ki
70o ~ 21Fe-2V-III

It can be readily seen from Table 4- that the effects of adding these metallic elements on magnetic properties, in particular on the rectangular course of the hysteresis curve, are quite different, although all samples could be expected to improve both the magnetic properties , as well as increasing the specific electrical resistance,

For Fe-Co-lTi alloys, copper and molybdenum have proven to be the proved to be the most preferable additives, not only in terms of increasing the specific electrical resistance, but also because of the improvement of the rectangular shape of the hysteresis curve through magnetic annealing treatment.

Example 5

A core was made in the form of a laminate of U-shaped core elements compiled as shown in Fig. 4-. They were made from a plate or sheet metal or sheets of the Composition of the sample Kr. 3 or Kr. 10 punched, their properties are given in Table 1. A core element after

BATH ORIGINAL

Fig. 4 has a thickness of about 0.3 ram, 1, is given for four different lengths in G? A.belle 5, Ip = 10 mm, I ₇ «■ 20 mm and I ₂ ,« 5 mm.

'^; After the punching, a core element was tempered at high temperature and then in a magnetic field from 700 ° 0 to 40 ° 0 at a cooling rate of 100 ° C / hour. annealed. The magnetic annealing took place as shown in FIG. 5, in which a winding is denoted by 1, a U-shaped laminated core is denoted by 2 and a ceramic cylinder is denoted by 3, around which the coil 1 is wound. The legs of each core element were alternately inserted into the ceramic cylinders from opposite sides to form a frame-shaped core.

A voltage was applied to the coil so that a magnetic field of 4 oersted was formed in it. After finishing the magnetic The kernel components were removed from the skin treatment and 30 of them were put together to form a core laminate or package, where the open ends of the legs of each core "e ^ jßmont * at the closed ends of the legs of the other kernels some have been stacked, as shown in Fig. 6, "In this Figure öind the lines 4 to the solenoid coils with 5 parts * laminated U-shaped Ktpn with 6 and the insulating layers denoted by 7.

The magnetic properties of these laminated cores are in 'of Table 5.

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Table 5

sample
No. Magnetic
properties s »50 mm Leg length
= 55 mm = 70 mm 12.1 = 100 mn 5 BIO (KG) 12.0 12.1 89.7 12.1 Br / 310 (Si) 85.0 88.5 95.5 89.4 BO.5 / B1O (55) 90.4 95.7 0.057 96.0 Hc (Oe) 0.036 0.057 •
11.4 0.058 10 BIO (KG) 11.5 11.4 87.5 11.4 Br / BlO (#) ■ 80.2 86.5 95.2 67.0 BO.5 / B1O (0) 88.1 92.9 0.051 94.0 Hc (Oe) 0.050 0.050 0.054

A comparison of Table 1 with Table 5 shows that the rectangular course of the hysteresis curve of the laminated U-shaped Kernes is vrenig worse than with the toroidal core. The cause for this are small gaps created at the opposite ends of the legs of the laminated core by alternative lamination of the U-shaped core elements in opposite directions have arisen.

If 1, of the laminated core is larger than 55 mm, however, the rectangular shape of its hysteresis curve is such that Br / BlO> 85 & and BO.5 / BIO> 90 # and are suitable as a core for a magnetic amplifier or magnetic multivibrator .

Table 5 shows that with increasing I ₁

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the Kechteclc ratio as well as its coercive force tend to be inclined to rise. It could also be determined that the
The ratio of the leg length 1 to the length 1 of the yoke should be at least 2.5 and preferably in the range from 5 to 5
lies.

Compared to conventional ring cores, a laminated core according to the invention has the further advantage that it only slightly prevents its magnetic properties in the event of external tensions or external stresses. As an experiment, one has an external force with an amplitude of $ g, where g is the acceleration due to gravity, on a U ~ for a day and a half
shaped core according to the invention and let act on an annular core made of oriented 50-Pernalloy with a thickness of 0.1 mm. Although the pike-corner ratio of the ring core decreased by 5-7 ^{° C} , no change in magnetic properties could be observed on the core according to the invention.

Pa.t claims

Claims (5)

Patontans ρ r ü c he 1 »Magnetic alloy, consisting of about 30 wt. # Cobalt, up to about 30 wt. fa iron, up to about 6 wt. # copper and / or molybdenum, Eest Kiekel. 2. Alloy according to claim 1, characterized in that that they are 1.5 to 4 wt. # copper and / or molybdenum contains, '■ 3 «alloy according to claim 1, characterized in that it comprises about 50 to 80 wt.% Wraps, about 5-30 wt. # Cobalt and about 10 to 30 GeV /. # Contains iron. 4. Alloy according to claim 1, characterized in that it is 7 to 21 Gev /. ^c , j cobalt, 20 to 25 Gev /. ^c ,!> quiet, 1.5 to 4 Gev /. £ molybdenum and / or copper, remainder ' Contains Hiekel. ■ 5. Alloy according to claim 1 to 4, characterized in that that they have an Ourie point greater than 620 ° 0 BATH ORIQINAL - 20 ~ 209813/0266 Blank page